Selective deposition

ABSTRACT

A method for epitaxially forming a silicon-containing material on a substrate surface utilizes a halogen containing gas as both an etching gas as well as a carrier gas through adjustments of the process chamber temperature and pressure. It is beneficial to utilize HCl as the halogen containing gas because converting HCl from a carrier gas to an etching gas can easily be performed by adjusting the chamber pressure.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a continuation-in-part of U.S. patent application Ser. No. 11/001,774, now issued as U.S. Pat. No. 7,312,128, filed Dec. 1, 2004, which is herein incorporated by reference. This application is related to U.S. patent application Ser. No. 11/421,156, filed May 31, 2006 and U.S. patent application Ser. No. 11/745,416, filed May 7, 2007.

BACKGROUND OF THE INVENTION

1. Field of the Invention

Embodiments of the present invention relates to the field of electronic manufacturing processes and devices, more particularly, to methods of depositing silicon-containing films while forming electronic devices.

2. Description of the Related Art

As smaller transistors are manufactured, ultra shallow source/drain junctions are becoming more challenging to produce. Sub-100 nm CMOS (complementary metal-oxide semiconductor) devices require a junction depth to be less than 30 nm. Selective epitaxial deposition is often utilized to form epilayers of silicon-containing materials (e.g., Si, SiGe and SiC) into the junctions. Selective epitaxial deposition permits growth of epilayers on silicon moats with no growth on dielectric areas. Selective epitaxy can be used within semiconductor devices, such as elevated source/drains, source/drain extensions, contact plugs or base layer deposition of bipolar devices.

A selective epitaxy process involves a deposition reaction and an etch reaction. The deposition and etch reactions occur simultaneously with relatively different reaction rates to an epitaxial layer and to a polycrystalline layer. During the deposition process, the epitaxial layer is formed on a monocrystalline surface while a polycrystalline layer is deposited on at least a second layer, such as an existing polycrystalline layer and/or an amorphous layer. However, the deposited polycrystalline layer is etched at a faster rate than the epitaxial layer. Therefore, by changing the concentration of an etchant gas, the net selective process results in deposition of epitaxy material and limited, or no, deposition of polycrystalline material. For example, a selective epitaxy process may result in the formation of an epilayer of silicon-containing material on a monocrystalline silicon surface while no deposition is left on the spacer.

Selective epitaxy deposition of silicon-containing materials has become a useful technique during formation of elevated source/drain and source/drain extension features, for example, during the formation of silicon-containing MOSFET (metal oxide semiconductor field effect transistor) devices. Source/drain extension features are manufactured by etching a silicon surface to make a recessed source/drain feature and subsequently filling the etched surface with selectively grown epilayers, such as a silicon germanium (SiGe) material. Selective epitaxy permits near complete dopant activation with in-situ doping, so that the post annealing process is omitted. Therefore, junction depth can be defined accurately by silicon etching and selective epitaxy. On the other hand, the ultra shallow source/drain junction inevitably results in increased series resistance. Also, junction consumption during silicide formation increases the series resistance even further. In order to compensate for junction consumption, an elevated source/drain is epitaxially and selectively grown on the junction. Typically, the elevated source/drain layer is undoped silicon.

However, current selective epitaxy processes have some drawbacks. In order to maintain selectivity during present epitaxy processes, chemical concentrations of the precursors, as well as reaction temperatures must be regulated and adjusted throughout the deposition process. If not enough silicon precursor is administered, then the etching reaction may dominate and the overall process is slowed down. Also, harmful over etching of substrate features may occur. If not enough etchant precursor is administered, then the deposition reaction may dominate reducing the selectivity to form monocrystalline and polycrystalline materials across the substrate surface. Also, current selective epitaxy processes usually require a high reaction temperature, such as about 800° C., 1,000° C. or higher. Such high temperatures are not desirable during a fabrication process due to thermal budget considerations and possible uncontrolled nitridation reactions to the substrate surface.

Therefore, there is a need to have a process for selectively and epitaxially depositing silicon and silicon-containing compounds with optional dopants. Furthermore, the process should be versatile to form silicon-containing compounds with varied elemental concentrations while having a fast deposition rate.

SUMMARY OF THE INVENTION

The present invention provides a method of epitaxially depositing a layer on a substrate. A method for epitaxially forming a silicon-containing material on a substrate surface utilizes halogen containing gas as both an etching gas as well as a carrier gas through adjustments of the process chamber temperature and the pressure. It is beneficial to utilize HCl as the halogen containing gas because converting HCl from a carrier gas to an etching gas can easily be performed by adjusting the chamber pressure.

In a first embodiment, a method of epitaxially forming a silicon-containing material on a substrate surface is disclosed. The method involves positioning into a process chamber a substrate having a monocrystalline surface and at least a second surface. The second surface can be an amorphous surface, a polycrystalline surface or combinations thereof. The substrate is exposed to a deposition gas to deposit an epitaxial layer on the monocrystalline surface and a polycrystalline layer on the second surface. The deposition gas has a silicon source and a carrier gas comprising a halogen containing compound. Subsequently the substrate is exposed to an etching gas to etch the polycrystalline layer and the epitaxial layer. The polycrystalline layer is etched at a faster rate than the epitaxial layer.

According to one aspect of the first embodiment, the halogen containing compound comprises HCl and HCl is used as both a carrier gas during deposition and an etching gas.

According to another aspect of the first embodiment, a halogen containing gas is used as a carrier gas during deposition but an etching gas comprising chlorinated hydrocarbon is used.

In a second embodiment, a method of epitaxially forming a silicon-containing material on a substrate positioned in a process chamber is disclosed. The substrate includes a monocrystalline surface and a second surface selected from the group consisting of an amorphous surface, a polycrystalline surface and combinations thereof. The method involves controlling a flow of halogen containing gas into the process chamber to a first flow rate to deposit an epitaxial layer on the monocrystalline surface and a polycrystalline layer on the second surface, and controlling a flow rate of halogen containing gas into the process chamber to a second flow rate to etch the polycrystalline layer and the epitaxial layer.

BRIEF DESCRIPTION OF THE DRAWINGS

So that the manner in which the above recited features of the present invention can be understood in detail, a more particular description of the invention, briefly summarized above, may be had by reference to embodiments, some of which are illustrated in the appended drawings. It is to be noted, however, that the appended drawings illustrate only typical embodiments of this invention and are therefore not to be considered limiting of its scope, for the invention may admit to other equally effective embodiments.

FIG. 1 is a flow chart describing a process to selectively and epitaxially deposit silicon-containing materials in one embodiment described herein;

FIGS. 2A-2E show schematic illustrations of fabrication techniques for a source/drain extension device within a MOSFET;

FIGS. 3A-C show several devices containing selectively and epitaxially deposited silicon-containing layers by applying embodiments described herein;

FIG. 4 is a flow chart describing a process to selectively and epitaxially deposit silicon-containing materials in another embodiment described herein; and

FIGS. 5A-5C are graphs showing the HCl flow rates, total pressure, and source gas flow rates versus time.

DETAILED DESCRIPTION

Embodiments of the invention provide processes to selectively and epitaxially deposit silicon-containing materials on monocrystalline surfaces of a substrate during fabrication of electronic devices. A patterned substrate containing a monocrystalline surface (e.g., silicon or silicon germanium) and at least a secondary surface, such as an amorphous surface and/or a polycrystalline surface (e.g., oxide or nitride), is exposed to an epitaxial process to form an epitaxial layer on the monocrystalline surface while forming limited or no polycrystalline layer on the secondary surfaces. The epitaxial process, also referred to as the alternating gas supply (AGS) process, includes repeating a cycle of a deposition process and an etching process until the desired thickness of an epitaxial layer is grown.

The deposition process includes exposing the substrate surface to a deposition gas containing at least a silicon source and a carrier gas. The deposition gas may also include a germanium source or carbon source, as well as a dopant source. During the deposition process, an epitaxial layer is formed on the monocrystalline surface of the substrate while a polycrystalline layer is formed on secondary surfaces, such as amorphous and/or polycrystalline surfaces. Subsequently, the substrate is exposed to an etching gas. The etching gas includes a carrier gas and an etchant, such as chlorine gas or hydrogen chloride. The etching gas removes silicon-containing materials deposited during the deposition process. During the etching process, the polycrystalline layer is removed at a faster rate than the epitaxial layer. Therefore, the net result of the deposition and etching processes forms epitaxially grown silicon-containing material on monocrystalline surfaces while minimizing growth, if any, of polycrystalline silicon-containing material on the secondary surfaces. A cycle of the deposition and etching processes may be repeated as needed to obtain the desired thickness of silicon-containing materials. The silicon-containing materials which can be deposited by embodiments of the invention include silicon, silicon germanium, silicon carbon, silicon germanium carbon, and dopant variants thereof.

In general, deposition processes may be conducted at lower temperatures than etching reactions, since etchants often need a high temperature to be activated. For example, silane may be thermally decomposed to deposit silicon at about 500° C. or less, while hydrogen chloride requires an activation temperature of about 700° C. or higher to act as an effective etchant. Therefore, if hydrogen chloride is used during an AGS process, the overall process temperature is dictated by the higher temperature required to activate the etchant.

In one example of an AGS process, an inert gas, such as a noble gas or nitrogen, is used as a carrier gas during the deposition and etching processes, instead of a traditional carrier gas, such as hydrogen. The use of an inert carrier gas has several attributes during an AGS process. For one, an inert carrier gas may increase the deposition rate of the silicon-containing material. While hydrogen may be used as a carrier gas, during the deposition process, hydrogen has a tendency to adsorb or react to the substrate to form hydrogen-terminated surfaces. A hydrogen-terminated surface reacts much slower to epitaxial growth than a bare silicon surface. Therefore, the use of an inert carrier gas increases the deposition rate by not adversely effecting the deposition reaction.

It has been found that a halogen containing gas can be used as the carrier gas. Under very specific conditions, the halogen containing gas will not etch the material. The halogen containing gas will act as an inert gas. The benefit of using the halogen containing gas as a carrier gas is that the halogen containing gas can be tailored for use as an etchant during the etching phase or as an inert carrier gas for the deposition phase. The tailoring of the halogen containing gas for either use is controlled by the temperature and pressure. By keeping the halogen containing gas below the etching threshold, the halogen containing gas will function as an effective carrier gas. The etching threshold varies depending upon the specific halogen containing gas used.

Diatomic halogens could be used, but they need to be used at low process chamber temperatures (i.e. less than about 550° C.) and very low concentrations. It is possible to use a mixture of a diatomic halogen and a halogen containing gas. Preferably the halogen containing gas is selected from HCl, HBr, and HI, with HCl being most preferred. A small amount of Cl₂ can be added to the HCl to increase the reactivity of the HCl during the etching phase. A small amount of H₂ or N₂ or any inert gas such as Ar or He can be added to control the reactivity of the HCl for the deposition phase. The specific parameters include a process chamber operating temperature of between about 500° C. and about 650° C. and a process chamber operating pressure of about 1 Torr to about 100 Torr. The benefits of using HCl instead of Cl₂ are several. HCl does not attack the growing film as much as Cl₂. HCl more selectively etches. There are fewer defects on the resulting film using HCl as opposed to Cl₂.

At the processing chamber deposition temperatures (i.e. between about 500° C. and about 650° C.), HCl etch efficiency is normally drastically reduced. Thus, for the processing chamber deposition temperatures of 500° C.-650° C., HCl acts as an inert gas. When operating at these low processing chamber temperatures, HCl will not etch efficiently. To etch using HCl at these low processing chamber temperatures, it is necessary to increase the pressure.

By modulating the HCl flow between low (i.e. about 60 to about 600 sccm) and high (i.e. about 2,000 to about 20,000 sccm), an alternating deposition/etching cycle is achieved. The deposition step is an inefficient etch, or growth step where the HCl flow is low. The efficient etch step occurs at high HCl flow. By modulating the flow, high pressure etching is performed between the low pressure deposition steps with little change in the pumping speed. The pressure control is not greatly burdened. FIGS. 5A-5C show the comparison of the HCl flow, total chamber pressure, and source gas flow over time. Source gas is provided to the chamber during the deposition phase. HCl gas is constantly provided, but during the deposition phase, the HCl is provided at a lower flow rate (i.e. about 60 to about 600 sccm). The total chamber pressure during the deposition phase is about 1 to about 100 Torr. A small amount of etching may occur during the deposition phase, but it will be minimal. During the etching phase, the source gas is shut off and the HCl gas flow is increased (i.e. about 2,000 to about 20,000 sccm). The total chamber pressure is increased to about 30 to about 100 Torr. During the etch phase, no deposition will occur. The deposition phase and the etching phase are about equal in length. The deposition phase lasts for about 5 to about 25 seconds and the etching phase lasts about 10 to about 30 seconds. The source gas can contain Si, Ge, C, and combinations thereof.

Sometimes, it is preferable to operate at low chamber deposition temperatures (i.e. about 500° C. to about 650° C.), but also at low chamber pressures (i.e. less than about 50 Torr). At low pressures, however, HCl will not effectively etch. Adding Cl₂ at the low temperatures and pressures is not an option because it is too aggressive. Chlorinated hydrocarbons are an attractive alternative.

By chlorinated hydrocarbon, it is understood to comprise a hydrocarbon containing a C—Cl bond. Examples of exemplary chlorinated hydrocarbons includes chloroalkyls (i.e. methyl chloride, dichloromethane, chloroform, carbon tetrachloride, ethyl chloride, etc.), chloroalkenes, chlorine substituted phenyls, and chloroalkynes, for example.

In order for a chlorinated hydrocarbon to be effective at etching silicon based films, the C—Cl bond strength should be weaker than the Si—Cl bond strength so that the chlorine will be substitutional and not interstitial. The nature of the hydrocarbon to which Cl is bonded determines the bond strength of the available chlorine. The chlorinated hydrocarbon can be used with any silicon and carbon source gas either simultaneously (i.e. co-flowed) or alternately (i.e. cyclic deposition/etching scheme). The chlorinated hydrocarbon can be used at any process chamber temperature or pressure. The chlorinated hydrocarbon can be a gas, liquid, or solid, but preferably is has a high vapor pressure. Also the chlorinated hydrocarbon should be of a high purity.

In the above example, the chlorinated hydrocarbon is used as an etchant in a process where HCl is used as an inert carrier gas during the deposition phase. However, the chlorinated hydrocarbon may be used as an etchant in combination with any inert carrier or background gas during the deposition phase. The chlorinated hydrocarbon enables the etching phase to occur at process chamber pressures of about 50 Torr or less.

Throughout the application, the terms “silicon-containing” materials, compounds, films or layers should be construed to include a composition containing at least silicon and may contain germanium, carbon, boron, arsenic, phosphorous gallium and/or aluminum. Other elements, such as metals, halogens or hydrogen may be incorporated within a silicon-containing material, compound, film or layer, usually in part per million (ppm) concentrations. Compounds or alloys of silicon-containing materials may be represented by an abbreviation, such as Si for silicon, SiGe, for silicon germanium, SiC for silicon carbon and SiGeC for silicon germanium carbon. The abbreviations do not represent chemical equations with stoichiometrical relationships, nor represent any particular reduction/oxidation state of the silicon-containing materials.

FIG. 1 illustrates an example of epitaxial process 100 used to deposit a silicon-containing layer. The process 100 includes step 110 for loading a patterned substrate into a process chamber and adjusting the conditions within the process chamber to a desired temperature and pressure. Step 120 provides a deposition process to form an epitaxiai layer on a monocrystalline surface of the substrate while forming a polycrystalline layer on the amorphous and/or polycrystalline surfaces of the substrate. During step 130, the deposition process is terminated. Step 140 provides an etching process to etch the surface of the substrate. Preferably, the polycrystalline layer is etched at a faster rate than the epitaxial layer. The etching step either minimizes or completely removes the polycrystalline layer while removing only a marginal portion of the epitaxial layer. During step 150, the etching process is terminated. The thickness of the epitaxial layer and the polycrystalline layer, if any, is determined during step 160. If the predetermined thickness of the epitaxial layer or the polycrystalline layer is achieved, then epitaxial process 100 is terminated at step 170. However, if the predetermined thickness is not achieved, then steps 120-160 are repeated as a cycle until the predetermined thickness is achieved.

A patterned substrate is loaded into a process chamber during step 110. Patterned substrates are substrates that include electronic features formed into or onto the substrate surface. The patterned substrate usually contains monocrystalline surfaces and at least one secondary surface that is non-monocrystalline, such as polycrystalline or amorphous surfaces. Monocrystalline surfaces include the bare crystalline substrate or a deposited single crystal layer usually made from a material such as silicon, silicon germanium or silicon carbon. Polycrystalline or amorphous surfaces may include dielectric materials, such as oxides or nitrides, specifically silicon oxide or silicon nitride, as well as amorphous silicon surfaces.

Epitaxial process 100 begins by adjusting the process chamber containing the patterned substrate to a predetermined temperature and pressure during step 110. The temperature is tailored to the particular conducted process. The process chamber is maintained at a consistent temperature throughout epitaxial process 100. However, some steps may be performed at varying temperatures. The process chamber is kept at a temperature in the range from about 250° C. to about 1,000° C., preferably from about 500° C. to about 800° C. and more preferably from about 550° C. to about 750° C. The appropriate temperature to conduct epitaxial process 100 may depend on the particular precursors used to deposit and/or etch the silicon-containing materials during steps 120 and 140. When using HCl as both a carrier gas and as an etching gas, the process chamber pressure switches between a defined high pressure during the etching step and a defined low pressure during the deposition step.

The deposition process is conducted during step 120. The patterned substrate is exposed to a deposition gas to form an epitaxial layer on the monocrystalline surface while forming a polycrystalline layer on the secondary surfaces. The substrate is exposed to the deposition gas for a period of time of about 0.5 seconds to about 30 seconds, preferably from about 5 seconds to about 25 seconds. The specific exposure time of the deposition process is determined in relation to the exposure time during the etching process in step 140, as well as particular precursors and temperature used in the process. The substrate is exposed to the deposition gas long enough to form a maximized thickness of an epitaxial layer while forming a minimal thickness of a polycrystalline layer that may be easily etched away during subsequent step 140.

The deposition gas contains at least a silicon source and a carrier gas, and may contain at least one secondary elemental source, such as a germanium source and/or a carbon source. Also, the deposition gas may further include a dopant compound to provide a source of a dopant, such as boron, arsenic, phosphorous, gallium and/or aluminum.

The silicon source is usually provided into the process chamber at a rate in a range from about 5 sccm to about 500 sccm, preferably from about 10 sccm to about 300 sccm, and more preferably from about 50 sccm to about 200 sccm, for example, about 100 sccm. Silicon sources useful in the deposition gas to deposit silicon-containing compounds include silanes, halogenated silanes and organosilanes. Silanes include silane (SiH₄) and higher silanes with the empirical formula Si_(x)H_((2x+2)), such as disilane (Si₂H₆), trisilane (Si₃H₈), and tetrasilane (Si₄H₁₀), as well as others. Halogenated silanes include compounds with the empirical formula X′_(y)Si_(x)H_((2x+2-y)), where X′=F, Cl, Br or I, such as hexachlorodisilane (Si₂Cl₆), tetrachlorosilane (SiCl₄), dichlorosilane (Cl₂SiH₂) and trichlorosilane (Cl₃SiH). Organosilanes include compounds with the empirical formula R_(y)Si_(x)H_((2x+2-y)), where R=methyl, ethyl, propyl or butyl, such as methylsilane ((CH₃)SiH₃), dimethylsilane ((CH₃)₂SiH₂), ethylsilane ((CH₃CH₂)SiH₃), methyldisilane ((CH₃)Si₂H₅), dimethyldisilane ((CH₃)₂Si₂H₄) and hexamethyldisilane ((CH₃)₆Si₂). Organosilane compounds have been found to be advantageous silicon sources as well as carbon sources in embodiments which incorporate carbon in the deposited silicon-containing compound. The preferred silicon sources include silane, dichlorosilane and disilane.

The silicon source is usually provided into the process chamber along with a carrier gas. The carrier gas has a flow rate from about 60 to about 600 sccm. Carrier gases may include nitrogen (N₂), hydrogen (H₂), argon, helium and combinations thereof. HCl is the preferred carrier gas. A carrier gas may be selected based on the precursor(s) used and/or the process temperature during the epitaxial process 100. Usually the carrier gas is the same throughout each of the steps 110-150. However, some embodiments may use different carrier gases in particular steps. HCl may be used as a carrier gas with the silicon source in step 120 and with the etchant in step 140.

The deposition gas used during step 120 may also contain at least one secondary elemental source, such as a germanium source and/or a carbon source. The germanium source may be added to the process chamber with the silicon source and carrier gas to form a silicon-containing compound, such as a silicon germanium material. The germanium source is usually provided into the process chamber at a rate in the range from about 0.1 sccm to about 20 sccm, preferably from about 0.5 sccm to about 10 sccm, and more preferably from about 1 sccm to about 5 sccm, for example, about 2 sccm. Germanium sources useful to deposit silicon-containing compounds include germane (GeH₄), higher germanes and organogermanes. Higher germanes include compounds with the empirical formula Ge_(x)H_((2x+2)), such as digermane (Ge₂H₆), trigermane (Ge₃H₈) and tetragermane (Ge₄H₁₀), as well as others. Organogermanes include compounds such as methylgermane ((CH₃)GeH₃), dimethylgermane ((CH₃)₂GeH₂), ethylgermane ((CH₃CH₂)GeH₃), methyldigermane ((CH₃)Ge₂H₅), dimethyldigermane ((CH₃)₂Ge₂H₄) and hexamethyldigermane ((CH₃)₆Ge₂). Germanes and organogermane compounds have been found to be advantageous germanium sources and carbon sources in embodiments while incorporating germanium and carbon into the deposited silicon-containing compounds, namely SiGe and SiGeC compounds. The germanium concentration in the epitaxial layer is in the range from about 1 at % to about 30 at %, for example, about 20 at %. The germanium concentration may be graded within an epitaxial layer, preferably graded with a higher germanium concentration in the lower portion of the epitaxial layer than in the upper portion of the epitaxial layer.

Alternatively, a carbon source may be added during step 120 to the process chamber with the silicon source and carrier gas to form a silicon-containing compound, such as a silicon carbon material. A carbon source is usually provided into the process chamber at a rate in the range from about 0.1 sccm to about 20 sccm, preferably from about 0.5 sccm to about 10 sccm, and more preferably from about 1 sccm to about 5 sccm, for example, about 2 sccm. Carbon sources useful to deposit silicon-containing compounds include organosilanes, alkyls, alkenes and alkynes of ethyl, propyl and butyl. Such carbon sources include methylsilane (CH₃SiH₃), dimethylsilane ((CH₃)₂SiH₂), ethylsilane (CH₃CH₂SiH₃), methane (CH₄), ethylene (C₂H₄), ethyne (C₂H₂), propane (C₃H₈), propene (C₃H₆), butyne (C₄H₆), as well as others. The carbon concentration of an epitaxial layer is in the range from about 200 ppm to about 5 at %, preferably from about 1 at % to about 3 at %, for example 1.5 at %. In one embodiment, the carbon concentration may be graded within an epitaxial layer, preferably graded with a higher carbon concentration in the lower portion of the epitaxial layer than in the upper portion of the epitaxial layer. Alternatively, a germanium source and a carbon source may both be added during step 120 into the process chamber with the silicon source and carrier gas to form a silicon-containing compound, such as a silicon germanium carbon material.

The deposition gas used during step 120 may further include at least one dopant compound to provide a source of elemental dopant, such as boron, arsenic, phosphorous, gallium or aluminum. Dopants provide the deposited silicon-containing compounds with various conductive characteristics, such as directional electron flow in a controlled and desired pathway required by the electronic device. Films of the silicon-containing compounds are doped with particular dopants to achieve the desired conductive characteristic. In one example, the silicon-containing compound is doped p-type, such as by using diborane to add boron at a concentration in the range from about 10¹⁵ atoms/cm³ to about 10²¹ atoms/cm³. In one example, the p-type dopant has a concentration of at least 5×10¹⁹ atoms/cm³. In another example, the p-type dopant is in the range from about 1×10²⁰ atoms/cm³ to about 2.5×10²¹ atoms/cm³. In another example, the silicon-containing compound is doped n-type, such as with phosphorous and/or-arsenic to a concentration in the range from about 10¹⁵ atoms/cm³ to about 10²¹ atoms/cm³.

A dopant source is usually provided into the process chamber during step 120 at a rate in the range from about 0.1 sccm to about 20 sccm, preferably from about 0.5 sccm to about 10 sccm, and more preferably from about 1 sccm to about 5 sccm, for example, about 2 sccm. Boron-containing dopants useful as a dopant source include boranes and organoboranes. Boranes include borane, diborane (B₂H₆), triborane, tetraborane and pentaborane, while alkylboranes include compounds with the empirical formula R_(x)BH_((3-x)), where R=methyl, ethyl, propyl or butyl and x=1, 2 or 3. Alkylboranes include trimethylborane ((CH₃)₃B), dimethylborane ((CH₃)₂BH), triethylborane ((CH₃CH₂)₃B) and diethylborane ((CH₃CH₂)₂BH). Dopants may also include arsine (AsH₃), phosphine (PH₃) and alkylphosphines, such as with the empirical formula R_(x)PH_((3-x)), where R=methyl, ethyl, propyl or butyl and x=1, 2 or 3. Alkylphosphines include trimethylphosphine ((CH₃)₃P), dimethylphosphine ((CH₃)₂PH), triethylphosphine ((CH₃CH₂)₃P) and diethylphosphine ((CH₃CH₂)₂PH). Aluminum and gallium dopant sources may include alkylated and/or halogenated derivates, such as described with the empirical formula R_(x)MX_((3-x)), where M=Al or Ga, R=methyl, ethyl, propyl or butyl, X═Cl or F and x=0, 1, 2 or 3. Examples of aluminum and gallium dopant sources include trimethylaluminum (Me₃Al), triethylaluminum (Et₃Al), dimethyiaiuminumchioride (Me₂AlCl), aluminum chloride (AlCl₃), trimethylgallium (Me₃Ga), triethylgallium (Et₃Ga), dimethylgalliumchloride (Me₂GaCl) and gallium chloride (GaCl₃).

During step 130, the deposition process is terminated. In one example, the process chamber may be flushed with a purge gas or the carrier gas and/or the process chamber may be evacuated with a vacuum pump. The purging and/or evacuating processes remove excess deposition gas, reaction by-products and other contaminates. In another example, once the deposition process has terminated, the etching process in step 140 is immediately started without purging and/or evacuating the process chamber.

The etching process in step 140 removes silicon-containing materials deposited during step 120 from the substrate surface. The etching process removes both epitaxial or monocrystalline materials and amorphous or polycrystalline materials. Polycrystalline layers, if any, deposited on the substrate surface are removed at a faster rate than the epitaxial layers. The time duration of the etching process is balanced with the time duration of the deposition process to result in net deposition of the epitaxial layer selectively formed on desired areas of the substrate. Therefore, the net result of the deposition process in step 120 and etching process in step 140 is to form selective and epitaxially grown silicon-containing material while minimizing, if any, growth of polycrystalline silicon-containing material.

During step 140, the substrate is exposed to the etching gas for a period of time in the range from about 10 seconds to about 30 seconds. For a chlorinated carbon etchant it can be provided into the process chamber at a rate in the range from about 10 sccm to about 700 sccm, preferably from about 50 sccm to about 500 sccm, and more preferably from about 100 sccm to about 400 sccm, for example, about 200 sccm. For HCl, it can be provided at about 2,000 to about 20,000 sccm.

The etching process is terminated during step 150. In one example, the process chamber may be flushed with a purqe gas or the carrier gas and/or the process chamber may be evacuated with a vacuum pump. The purging and/or evacuating processes remove excess etching gas, reaction by-products and other contaminates. In another example, once the etching process has terminated, step 160 is immediately started without purging and/or evacuating the process chamber.

The thicknesses of the epitaxial layer and the polycrystalline layer may be determined during step 160. If the predetermined thicknesses are achieved, then epitaxial process 100 is terminated at step 170. However, if the predetermined thicknesses are not achieved, then steps 120-160 are repeated as a cycle until the desired thicknesses are achieved. The epitaxial layer is usually grown to have a thickness at a range from about 10 Å to about 2,000 Å, preferably from about 100 Å to about 1,500 Å, and more preferably from about 400 Å to about 1,200 Å, for example, about 800 Å. The polycrystalline layer is usually deposited with a thickness, if any, in a range from an atomic layer to about 500 Å. The desired or predetermined thickness of the epitaxial silicon-containing layer or the polycrystalline silicon-containing layer is specific to a particular fabrication process. In one example, the epitaxial layer may reach the predetermined thickness while the polycrystalline layer is too thick. The excess polycrystalline layer may be further etched by repeating steps 140-160 while skipping steps 120 and 130.

In one example, as depicted in FIGS. 2A-2E, a source/drain extension is formed within a MOSFET device wherein the silicon-containing layers are epitaxially and selectively deposited on the surface of the substrate. FIG. 2A depicts a source/drain region 232 formed by implanting ions into the surface of a substrate 230. The segments of source/drain region 232 are bridged by the gate 236 formed on gate oxide layer 235 and spacer 234. In order to form a source/drain extension, a portion of the source/drain region 232 is etched and wet-cleaned to produce a recess 238, as in FIG. 2B. Etching of the gate 236 may be avoided by depositing a hardmask prior to etching the portion of source/drain region 232.

FIG. 2C illustrates one embodiment of an epitaxial process described herein, in which a silicon-containing epitaxial layer 240 and optional polycrystalline layer 242 are simultaneously and selectively deposited without depositing on the spacer 234. Polycrystalline layer 242 is optionally formed on gate 236 by adjusting the deposition and etching processes in steps 120 and 140 of epitaxial process 100. Alternatively, polycrystalline layer 242 is continually etched away from gate 236 as epitaxial layer 240 is deposited on the source/drain region 232.

In another example, silicon-containing epitaxial layer 240 and polycrystalline layer 242 are SiGe-containing layers with a germanium concentration in a range from about 1 at % to about 50 at %, preferably about 24 at % or less. Multiple SiGe-containing layers containing varying amounts of silicon and germanium may be stacked to form silicon-containing epitaxial layer 240 with a graded elemental concentration. For example, a first SiGe-layer may be deposited with a germanium concentration in a range from about 15 at % to about 25 at % and a second SiGe-layer may be deposited with a germanium concentration in a range from about 25 at % to about 35 at %.

In another example, silicon-containing epitaxial layer 240 and polycrystalline layer 242 are SiC-containing layers with a carbon concentration in a range from about 200 ppm to about 5 at %, preferably about 3 at % or less, preferably, from about 1 at % to about 2 at %, for example, about 1.5 at %. In another embodiment, silicon-containing epitaxial layer 240 and polycrystalline layer 242 are SiGeC-containing layers with a germanium concentration in the range from about 1 at % to about 50 at %, preferably about 24 at % or less and a carbon concentration at about 200 ppm to about 5 at %, preferably about 3 at % or less, more preferably from about 1 at % to about 2 at %, for example, about 1.5 at %.

Multiple layers containing Si, SiGe, SiC or SiGeC may be deposited in varying order to form graded elemental concentrations within the silicon-containing epitaxial layer 240. The silicon-containing layers are doped with a dopant (e.g., boron, arsenic, phosphoric, gallium or aluminum) having a concentration in the range from about 1×10¹⁹ atoms/cm³ to about 2.5×10²¹ atoms/cm³, preferably from about 5×10¹⁹ atoms/cm³ to about 2×10²⁰ atoms/cm³. Dopants added to individual layers of the silicon-containing material form graded dopants. For example, silicon-containing epitaxial layer 240 is formed by depositing a first SiGe-containing layer with a dopant concentration (e.g., boron) in a range from about 5×10¹⁹ atoms/cm³ to about 1×10²⁰ atoms/cm³ and a second SiGe-containing layer with a dopant concentration (e.g., boron) in a range from about 1×10²⁰ atoms/cm³ to about 2×10²⁰ atoms/cm³.

Carbon incorporated in SiC-containing layers and SiGeC-containing layers is located in interstitial sites of the crystalline lattice immediately following the deposition of the silicon-containing layer. The interstitial carbon content is about 10 at % or less, preferably less than about 5 at % and more preferably from about 1 at % to about 3 at %, for example, about 2 at %. The silicon-containing epitaxial layer 240 may be annealed to incorporate at least a portion, if not all of the interstitial carbon into substitutional sites of the crystalline lattice. The annealing process may include a spike anneal, such as rapid thermal process (RTP), laser annealing or thermal annealing with an atmosphere of gas, such as oxygen, nitrogen, hydrogen, argon, helium or combinations thereof. The annealing process is conducted at a temperature from about 800° C. to about 1,200° C., preferably from about 1,050° C. to about 1,100° C. The annealing process may occur immediately after the silicon-containing layer is deposited or after a variety of other process steps the substrate will endure.

During the next step, FIG. 2D shows a spacer 244, a nitride spacer (e.g., Si₃N₄) deposited on the spacer 234. Spacer 244 is usually deposited in a different chamber by a CVD or ALD technique. Therefore, the substrate is removed from the process chamber that was used to deposit silicon-containing epitaxial layer 240. During the transfer between the two chambers, the substrate may be exposed to ambient conditions, such as the temperature, pressure or the atmospheric air containing water and oxygen. Upon depositing the spacer 244, or performing other semiconductor process (e.g., anneal, deposition or implant), the substrate may be exposed to ambient conditions a second time prior to depositing elevated layer 248. In one embodiment, an epitaxial layer (not shown) with no or minimal germanium (e.g., less than about 5 at %) is deposited on the top of epitaxial layer 240 before exposing the substrate to ambient conditions since native oxides are easier to remove from epitaxial layers containing minimal germanium concentrations than from an epitaxial layer formed with a germanium concentration greater than about 5 at %.

FIG. 2E depicts another example in which an elevated layer 248 comprised of a silicon-containing material is selectively and epitaxially deposited on epitaxial layer 240 (e.g., doped-SiGe). During the deposition process, polycrystalline layer 242 is further grown, deposited or etched away on the gate 236.

In a preferred embodiment, elevated layer 248 is epitaxial deposited silicon containing little or no germanium or carbon. However, in an alternative embodiment, elevated layer 248 does contain germanium and/or carbon. For example, elevated layer 248 may have about 5 at % or less of germanium. In another example, elevated layer 248 may have about 2 at % or less of carbon. Elevated layer 248 may also be doped with a dopant, such as boron, arsenic, phosphorous, aluminum or gallium.

Silicon-containing compounds are utilized within embodiments of the processes to deposit silicon-containing layers used for Bipolar device fabrication (e.g., base, emitter, collector, emitter contact), BiCMOS device fabrication (e.g., base, emitter, collector, emitter contact) and CMOS device fabrication (e.g., channel, source/drain, source/drain extension, elevated source/drain, substrate, strained silicon, silicon on insulator and contact plug). Other embodiments of processes teach the growth of silicon-containing layers that can be used as gate, base contact, collector contact, emitter contact, elevated source/drain and other uses.

The processes are extremely useful for depositing selective, epitaxial silicon-containing layers in MOSFET and bipolar transistors as depicted in FIGS. 3A-3C. FIGS. 3A-3B show the epitaxially grown silicon-containing compounds on a MOSFET device. The silicon-containing compound is deposited on the source/drain features of the device. The silicon-containing compound adheres and grows from the crystal lattice of the underlying layer and maintains this arrangement as the silicon-containing compound is grown to a desired thickness. FIG. 3A demonstrates the silicon-containing compound deposited as a recessed source/drain layer, while FIG. 3B shows silicon-containing compounds deposited as recessed source/drain layer and an elevated source/drain layer.

The source/drain region 312 is formed by ion implantation. The substrate 310 is doped n-type while the source/drain region 312 is doped p-type. Silicon-containing epitaxial layer 313 is selectively grown on the source/drain region 312 and/or directly on substrate 310. Silicon-containing epitaxial layer 314 is selectively grown on the silicon-containing layer 313 according to aspects herein. A gate oxide layer 318 bridges the segmented silicon-containing layer 313. Gate oxide layer 318 is composed of silicon dioxide, silicon oxynitride or hafnium oxide. Partially encompassing the gate oxide layer 318 is a spacer 316, which is usually an isolation material such as a nitride/oxide stack (e.g., Si₃N₄/SiO₂/Si₃N₄). Gate layer 322 (e.g., polysilicon) may have a protective layer 319, such as silicon dioxide, along the perpendicular sides, as in FIG. 3A. Alternately, gate layer 322 may have a spacer 316 and off-set layers 320 (e.g., Si₃N₄) disposed on either side.

In another example, FIG. 3C depicts the deposited silicon-containing epitaxial layer 334 as a base layer of a bipolar transistor. Silicon-containing epitaxial layer 334 is selectively grown with the various embodiments of the invention. Silicon-containing epitaxial layer 334 is deposited on an n-type collector layer 332 previously deposited on substrate 330. The transistor further includes isolation layer 333 (e.g., SiO₂ or Si₃N₄), contact layer 336 (e.g., heavily doped poly-Si), off-set layer 338 (e.g., Si₃N₄), and a second isolation layer 340 (e.g., SiO₂ or Si₃N₄).

In an alternative embodiment, FIG. 4 illustrates an epitaxial process 400 that may be used to selectively deposit silicon-containing materials/layer. Epitaxial process 400 includes at least two deposition processes followed by an etching process. The first deposition process includes a deposition gas containing a silicon source while the second deposition process includes a deposition gas containing a secondary elemental source, such as germanium, carbon or a dopant (e.g., boron, arsenic, phosphorous, gallium or aluminum). Similar process parameters used in epitaxial process 100 are used in epitaxial process 400, such as temperatures, pressures, flow rates, carrier gases and precursors.

Epitaxial process 400 includes step 410 for loading a patterned substrate into the process chamber and adjusting the process chamber to a predetermined temperature. Step 420 provides a first deposition process to form an epitaxial layer on a monocrystalline surface while forming a polycrystalline layer on secondary surfaces, such as amorphous and/or polycrystalline surfaces. The epitaxial layer and the monocrystalline layer are formed from a deposition gas containing a silicon source. During step 430, the first deposition process is terminated. Step 440 provides a second deposition process to continue growing the epitaxial layer on a monocrystalline surface and continue forming the polycrystalline layer on the secondary surface. The epitaxial layer and the polycrystalline layer are further grown by exposing the substrate surface to a deposition gas containing a secondary elemental source. At step 450, the second deposition process is terminated. Step 460 provides an etching process to etch the exposed silicon-containing layers. The etching process either minimizes or completely removes the polycrystalline layer while removing only a marginal portion of the epitaxial layer as a result of the rate at which each material is removed. During step 470, the etching process is terminated. The thicknesses of the epitaxial layer and the polycrystalline layer, if any, are determined during step 480. If the predetermined thickness is achieved, then epitaxial process 400 is terminated at step 490. However, if the predetermined thickness of either layer is not achieved, then steps 420-480 are repeated as a cycle until the predetermined thicknesses are achieved.

Epitaxial process 400 starts at step 410 by adjusting the process chamber containing the patterned substrate to a predetermined temperature. The temperature and pressure is tailored to the particular process conducted. The process chamber is maintained at a consistent temperature throughout epitaxial process 400. However, some steps may be performed at varying temperatures. The process chamber is kept at a temperature in the range from about 500° C. to about 650° C. The appropriate temperature to conduct epitaxial process 400 may depend on the particular precursors used to deposit and/or etch the silicon-containing materials during steps 420-480. The process chamber is usually maintained with a pressure from about 1 to about 100 Torr.

The first deposition process is conducted during step 420. The patterned substrate is exposed to a first deposition gas to form an epitaxial layer on the monocrystalline surface while forming a polycrystalline layer on the secondary surfaces. The substrate is exposed to the first deposition gas for a period of time of about 5 to about 25 seconds. The specific exposure time of the deposition process is determined in relation to the exposure time during the etching process in step 460, as well as particular precursors and temperature used in the process. The substrate is exposed to the first deposition gas long enough to form the maximized thickness of an epitaxial layer while forming the minimized thickness of a polycrystalline layer that may be easily etched away during subsequent step 460.

The first deposition gas contains at least a silicon source and a carrier gas. The first deposition gas may also contain a secondary elemental source and/or a dopant compound, but preferably, the secondary elemental source and the dopant compound are in the second deposition gas. Therefore, in one aspect, the first deposition gas may contain a silicon source, a secondary elemental source and a dopant source. In another aspect, the first deposition gas may contain a silicon source and a secondary elemental source. In yet another aspect, the first deposition gas may contain a silicon source and a dopant source. In an alternative embodiment, the first deposition gas may also include at least one etchant, such as hydrogen chloride or chlorine.

The silicon source is usually provided into the process chamber at a rate in the range from about 5 sccm to about 500 sccm, preferably from about 10 sccm to about 300 sccm, and more preferably from about 50 sccm to about 200 sccm, for example, about 100 sccm. The preferred silicon sources include silane, dichlorosilane and disilane.

The silicon source is usually provided into the process chamber in a carrier gas. The carrier gas has a flow rate from about 60 to about 600 sccm. Carrier gases may include nitrogen (N₂), hydrogen (H₂), argon, helium, HCl and combinations thereof. HCl is the preferred carrier gas because of its ability to function as an etchant or an inert under specific conditions.

During step 430, the first deposition process is terminated. In one example, the process chamber may be flushed with a purge gas or the carrier gas and/or the process chamber may be evacuated with a vacuum pump. The purging and/or evacuating processes remove excess deposition gas, reaction by-products and other contaminates. In another example, once the first deposition process has terminated, the second deposition process in step 440 is immediately started without purging and/or evacuating the process chamber.

The deposition gas used during step 440 contains a carrier gas and at least one secondary elemental source, such as a germanium source, a carbon source and/or a dopant compound. Alternatively, a silicon source may be included in the second deposition gas. The secondary elemental source is added to the process chamber with the carrier gas to continue the growth of the silicon-containing compounds deposited during step 420. The silicon-containing compounds may have varied compositions controlled by the specific secondary elemental source and the concentration of the secondary elemental source. A secondary elemental source is usually provided into the process chamber at a rate in the range from about 0.1 sccm to about 20 sccm, preferably from about 0.5 sccm to about 10 sccm, and more preferably from about 1 sccm to about 5 sccm, for example, about 2 sccm. Germanium sources, carbon sources and dopant compounds are selected from the aforementioned precursors discussed above.

During step 450, the second deposition process is terminated. In one example, the process chamber may be flushed with a purge gas or the carrier gas and/or the process chamber may be evacuated with a vacuum pump. The purging and/or evacuating processes remove excess deposition gas, reaction by-products and other contaminates. In another example, once the second deposition process has terminated, the etching process in step 460 is immediately started without purging and/or evacuating the process chamber.

The etching process in step 460 removes materials deposited during steps 420 and 440 from the substrate surface. The etching process removes both epitaxial or monocrystalline materials and amorphous and/or polycrystalline materials. Polycrystalline layers, if any, deposited on the substrate surface is removed at a faster rate than the epitaxial layers. The time duration of the etching process is balanced with the time duration of the two deposition processes. Therefore, the net result of the deposition processes in steps 420 and 440 and etching process in step 460 is to form selective and epitaxially grown silicon-containing material while minimizing, if any, growth of polycrystalline silicon-containing material. During step 460, the substrate is exposed to the etching gas for a period of time in a range from about 10 seconds to about 30 seconds.

The etching process is terminated during step 470. In one example, the process chamber may be flushed with a purge gas or the carrier gas and/or the process chamber may be evacuated with a vacuum pump. The purging and/or evacuating processes remove excess etching gas, reaction by-products and other contaminates. In another example, once the etching process has terminated, step 480 is immediately started without purging and/or evacuating the process chamber.

The thicknesses of epitaxial layer and the polycrystalline layer may be determined during step 480. If the predetermined thicknesses are achieved, then epitaxial process 400 is ended at step 490. However, if the predetermined thicknesses are not achieved, then steps 420-480 are repeated as a cycle until the desired thicknesses are achieved. The epitaxial layer is usually grown to have a thickness at a range from about 10 Å to about 2,000 Å, preferably from about 100 Å to about 1,500 Å, and more preferably from about 400 Å to about 1,200 Å, for example, about 800 Å. The polycrystalline layer is usually deposited to have a thickness, if any, at a range from about an atomic layer to about 500 Å. The desired or predetermined thickness of the epitaxial silicon-containing layer or the polycrystalline silicon-containing layer is specific to a particular fabrication process. In one example, the epitaxial layer may reach the predetermined thickness while the polycrystalline layer is too thick. The excess polycrystalline layer may be further etched by repeating steps 140-160 while omitting steps 460 and 470. Likewise, in other examples, steps 420, 440 and 460 may be individually omitted while proceeding through epitaxial process 400. By skipping steps 420, 440 and 460, the elemental concentration and the thicknesses of deposited silicon-containing materials may be controlled.

Embodiments of the invention teach processes to deposit silicon-containing compounds on a variety of substrates. Substrates on which embodiments of the invention may be useful include, but are not limited to semiconductor wafers, such as crystalline silicon (e.g., Si<100> and Si<111>), silicon oxide, silicon germanium, doped or undoped wafers and patterned or non-patterned wafers. Substrates have a variety of geometries (e.g., round, square and rectangular) and sizes (e.g., 200 mm OD, 300 mm OD).

In one embodiment, silicon-containing compounds deposited by process described herein include a germanium concentration within the range from about 0 at % to about 95 at %. In another embodiment, a germanium concentration is within the range from about 1 at % to about 30 at %, preferably from about 15 at % to about 30 at %, for example, about 20 at %. Silicon-containing compounds also include a carbon concentration within the range from about 0 at % to about 5 at %. In other aspects, a carbon concentration is within the range from about 200 ppm to about 3 at %, preferably about 1.5 at %.

The silicon-containing compound films of germanium and/or carbon are produced by various processes of the invention and can have consistent, sporadic or graded elemental concentrations. Graded silicon germanium films are disclosed in U.S. Pat. No. 6,770,134 and U.S. patent application Ser. No. 10/014,466, published as United States Patent Publication 20020174827, both assigned to Applied Materials, Inc., and are incorporated herein by reference in entirety for the purpose of describing methods of depositing graded silicon-containing compound films. In one example, a silicon source (e.g., SiH₄) and a germanium source (e.g., GeH₄) are used to selectively and epitaxially deposit silicon germanium containing films. In this example, the ratio of silicon source and germanium source can be varied in order to provide control of the elemental concentrations, such as silicon and germanium, while growing graded films. In another example, a silicon source and a carbon source (e.g., CH₃SiH₃) are used to selectively and epitaxially deposit silicon carbon containing films. The ratio of silicon source and carbon source can be varied in order to provide control of the elemental concentration while growing homogenous or graded films. In another example, a silicon source, a germanium source and a carbon source are used to selectively and epitaxially deposit silicon germanium carbon containing films. The ratios of silicon, germanium and carbon sources are independently varied in order to provide control of the elemental concentration while growing homogenous or graded films.

MOSFET devices formed by processes described herein may contain a PMOS component or a NMOS component. The PMOS component, with a p-type channel, has holes that are responsible for channel conduction, while the NMOS component, with a n-type channel, has electrons that are responsible channel conduction. Therefore, for example, a silicon-containing material such as SiGe may be deposited in a recessed area to form a PMOS component. In another example, a silicon-containing film such as SiC may be deposited in a recessed area to form a NMOS component. SiGe is used for PMOS application for several reasons. A SiGe material incorporates more boron than silicon alone, thus the junction resistivity may be lowered. Also, the SiGe/silicide layer interface at the substrate surface has a lower Schottky barrier than the Si/silicide interface.

Further, SiGe grown epitaxially on the top of silicon has compressive stress inside the film because the lattice constant of SiGe is larger than that of silicon. The compressive stress is transferred in the lateral dimension to create compressive strain in the PMOS channel and to increase mobility of the holes. For NMOS application, SiC can be used in the recessed areas to create tensile stress in the channel, since the lattice constant of SiC is smaller than that of silicon. The tensile stress is transferred into the channel and increases the electron mobility. Therefore, in one embodiment, a first silicon-containing layer is formed with a first lattice strain value and a second silicon-containing layer is formed with a second lattice strain value. For example, a SiC layer with a thickness from about 50 Å to about 200 Å is deposited on the substrate surface and sequentially, a SiGe layer with a thickness from about 150 Å to about 1,000 Å is deposited on the SiC layer. The SiC layer may be epitaxially grown and has less strain than the SiGe layer epitaxially grown on the SiC layer.

In embodiments described herein, silicon-containing compound films are selectively and epitaxially deposited by chemical vapor deposition (CVD) processes. Chemical vapor deposition processes include atomic layer deposition (ALD) processes and/or atomic layer epitaxy (ALE) processes. Chemical vapor deposition includes the use of many techniques, such as plasma-assisted CVD (PA-CVD), atomic layer CVD (ALCVD), organometallic or metalorganic CVD (OMCVD or MOCVD), laser-assisted CVD (LA-CVD), ultraviolet CVD (UV-CVD), hot-wire (HWCVD), reduced-pressure CVD (RP-CVD), ultra-high vacuum CVD (UHV-CVD) and others. In one embodiment, the preferred process is to use thermal CVD to epitaxially grow or deposit the silicon-containing compound, whereas the silicon-containing compound includes silicon, SiGe, SiC, SiGeC, doped variants thereof and combinations thereof.

The processes of the invention can be carried out in equipment known in the art of ALE, CVD and ALD. The apparatus may contain multiple gas lines to maintain the deposition gas and the etching gas separated prior to entering the process chamber. Thereafter, the gases are brought into contact with a heated substrate on which the silicon-containing compound films are grown. Hardware that can be used to deposit silicon-containing films includes the Epi Centurao system and the Poly Gene system available from Applied Materials, Inc., located in Santa Clara, Calif. An ALD apparatus is disclosed in U.S. Pat. Ser. No. 10/032,284, filed Dec. 21, 2001, published as United States Patent Publication No. 20030079686, assigned to Applied Materials, Inc., and entitled, “Gas Delivery Apparatus and Methods for ALD,” and is incorporated herein by reference in entirety for the purpose of describing the apparatus. Other apparatuses include batch, high-temperature furnaces, as known in the art.

The processes of the present invention can be performed by a computer readable program executable to perform the methods discussed above.

While the foregoing is directed to embodiments of the present invention, other and further embodiments of the invention may be devised without departing from the basic scope thereof, and the scope thereof is determined by the claims that follow. 

1. A method of epitaxially forming a silicon-containing material on a substrate surface, comprising: positioning into a process chamber a substrate comprising a monocrystalline surface and a second surface selected from the group consisting of an amorphous surface, a polycrystalline surface and combinations thereof; exposing the substrate to a deposition gas to deposit an epitaxial layer on the monocrystalline surface and a polycrystalline layer on the second surface, wherein the deposition gas comprises a silicon source and a carrier gas comprising a halogen containing compound at conditions adequate for the halogen containing compound to be non-reactive; and exposing the substrate to an etching gas to etch the polycrystalline layer and the epitaxial layer.
 2. The method as claimed in claim 1, wherein said halogen containing compound comprises HCl, HBr, HI, or combinations thereof.
 3. The method as claimed in claim 2, wherein said halogen containing compound comprises HCl.
 4. The method as claimed in claim 1, wherein the deposition gas additionally comprises Cl₂, H₂, N₂, an inert gas, or combinations thereof.
 5. The method as claimed in claim 1, wherein said halogen containing compound flows into said chamber at a rate of about 60 sccm to about 600 sccm during said exposing said substrate to said deposition gas.
 6. The method as claimed in claim 1, wherein said etching gas comprises said halogen containing compound at conditions adequate for the halogen containing compound to be an etching gas.
 7. The method as claimed in claim 6, wherein said halogen containing compound flows into said chamber alternately between a rate of about 60 sccm to about 600 sccm during said exposing said substrate to said deposition gas and a rate of about 2,000 sccm to about 20,000 sccm during said exposing said substrate to said etching gas.
 8. The method as claimed in claim 1, wherein a chamber pressure during said exposing the substrate to an etching gas is about 30 Torr to about 100 Torr.
 9. The method as claimed in claim 1, wherein a deposition cycle comprises repeating the exposing the substrate to the deposition gas and etching gas to form a silicon-containing material with a predetermined thickness.
 10. The method as claimed in claim 1, wherein the deposition cycle is repeated at least twice.
 11. The method as claimed in claim 1, wherein the epitaxial layer comprises a material selected from the group consisting of silicon-germanium, silicon-carbon, silicon-germanium-carbon and combinations thereof.
 12. The method as recited in claim 1, wherein the process chamber temperature is about 500° C. to about 650° C. during the exposing the substrate to a deposition gas and the exposing the substrate to an etching gas.
 13. A method of epitaxially forming a silicon-containing material on a substrate surface, comprising: positioning into a process chamber a substrate comprising a monocrystalline surface and a second surface selected from the group consisting of an amorphous surface, a polycrystalline surface and combinations thereof; exposing the substrate to a deposition gas to deposit an epitaxial layer on the monocrystalline surface and a polycrystalline layer on the second surface, wherein the deposition gas comprises a silicon source and a carrier gas comprising a halogen containing compound at conditions adequate for the halogen containing compound to be non-reactive; and exposing the substrate to a chlorinated hydrocarbon etching gas at a process chamber temperature below about 650° C. to etch the polycrystalline layer and the epitaxial layer.
 14. The method as claimed in claim 13, wherein said halogen containing compound comprises HCl, HBr, HI, or combinations thereof.
 15. The method as claimed in claim 14, wherein said halogen containing gas comprises HCl.
 16. The method as claimed in claim 13, wherein said chlorinated hydrocarbon comprises methyl chloride, dichloromethane, chloroform, carbon tetrachloride, ethyl chloride, a chloroalkene, or combinations thereof.
 17. The method as claimed in claim 13, wherein said chlorinated hydrocarbon is flowed to said chamber simultaneously with said deposition gas.
 18. The method as claimed in claim 13, wherein said chlorinated hydrocarbon is flowed to said chamber alternately with said deposition gas.
 19. The method as claimed in claim 13, wherein said exposing said substrate to said etching gas occurs at a process chamber pressure of about 50 Torr or less.
 20. The method as claimed in claim 13, wherein a deposition cycle comprises repeating the exposing the substrate to the deposition gas and etching gas to form a silicon-containing material with a predetermined thickness.
 21. The method as claimed in claim 20, wherein the deposition cycle is repeated at least twice.
 22. The method as claimed in claim 13, wherein the epitaxial layer comprises a material selected from the group consisting of silicon-germanium, silicon-carbon, silicon-germanium-carbon and combinations thereof.
 23. A method of epitaxially forming a silicon-containing material on a substrate surface, comprising: exposing the substrate to a deposition gas, wherein the deposition gas comprises a silicon source and HCl at conditions adequate for HCl to be a non-reactive carrier gas; and etching using HCl at conditions adequate to be an etching gas.
 24. The method as claimed in claim 23, wherein the deposition gas additionally comprises Cl₂, H₂, N₂, an inert gas, or combinations thereof.
 25. The method as claimed in claim 23, wherein said HCl flows into said chamber at a rate of about 60 sccm to about 600 sccm during said exposing said substrate to said deposition gas.
 26. The method as claimed in claim 23, wherein said HCl flows into said chamber at a rate of about 2,000 sccm to about 20,000 sccm during said etching.
 27. The method as claimed in claim 23, wherein said HCl flows into said chamber alternately between a rate of about 60 sccm to about 600 sccm during said exposing said substrate to said deposition gas and a rate of about 2,000 sccm to about 20,000 sccm during said etching.
 28. The method as recited in claim 23, wherein the process chamber temperature is about 500° C. to about 650° C. during the exposing the substrate to a deposition gas and the etching.
 29. A method of epitaxially forming a silicon-containing material on a substrate positioned in a process chamber, the substrate including a monocrystalline surface and a second surface selected from the group consisting of an amorphous surface, a polycrystalline surface and combinations thereof, said method comprising: controlling a flow of halogen containing gas into the process chamber to a first flow rate to deposit an epitaxial layer on the monocrystalline surface and a polycrystalline layer on the second surface, the halogen containing gas being at conditions adequate to be non-reactive; and controlling a flow rate of halogen containing gas into the process chamber to a second flow rate at conditions adequate to etch the polycrystalline layer and the epitaxial layer.
 30. The method as claimed in claim 29, wherein the halogen containing gas at the first flow rate and the halogen containing gas at the second flow rate are the same.
 31. The method as claimed in claim 30, wherein said halogen containing gas comprises HCl.
 32. The method as claimed in claim 31, wherein said halogen containing gas flows into said chamber at a rate of about 60 sccm to about 600 sccm for said first flow rate.
 33. The method as claimed in claim 31, wherein said halogen containing compound flows into said chamber at a rate of about 2,000 sccm to about 20,000 sccm for said second flow rate.
 34. The method as recited in claim 29, wherein the process chamber temperature is about 500° C. to about 650° C. during said method. 